EP2495057B1 - Outil de coupe revêtu en surface avec excellente résistance à l'écaillage - Google Patents

Outil de coupe revêtu en surface avec excellente résistance à l'écaillage Download PDF

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EP2495057B1
EP2495057B1 EP10826897.0A EP10826897A EP2495057B1 EP 2495057 B1 EP2495057 B1 EP 2495057B1 EP 10826897 A EP10826897 A EP 10826897A EP 2495057 B1 EP2495057 B1 EP 2495057B1
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Prior art keywords
layer
upper layer
lower layer
cutting
interface
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German (de)
English (en)
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EP2495057A1 (fr
EP2495057A4 (fr
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Makoto Igarashi
Kohei Tomita
Eiji Nakamura
Akira Osada
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Mitsubishi Materials Corp
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Mitsubishi Materials Corp
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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/02—Pretreatment of the material to be coated
    • C23C16/0272—Deposition of sub-layers, e.g. to promote the adhesion of the main coating
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
    • B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/02—Pretreatment of the material to be coated
    • C23C16/0272—Deposition of sub-layers, e.g. to promote the adhesion of the main coating
    • C23C16/029—Graded interfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/32—Carbides
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/34—Nitrides
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/36—Carbonitrides
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C16/00—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes
    • C23C16/22—Chemical coating by decomposition of gaseous compounds, without leaving reaction products of surface material in the coating, i.e. chemical vapour deposition [CVD] processes characterised by the deposition of inorganic material, other than metallic material
    • C23C16/30—Deposition of compounds, mixtures or solid solutions, e.g. borides, carbides, nitrides
    • C23C16/40—Oxides
    • C23C16/403—Oxides of aluminium, magnesium or beryllium
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
    • C23C28/044—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material coatings specially adapted for cutting tools or wear applications
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/04—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material
    • C23C28/048—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings of inorganic non-metallic material with layers graded in composition or physical properties
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T407/00—Cutters, for shaping
    • Y10T407/27—Cutters, for shaping comprising tool of specific chemical composition
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
    • Y10T428/24942—Structurally defined web or sheet [e.g., overall dimension, etc.] including components having same physical characteristic in differing degree
    • Y10T428/2495—Thickness [relative or absolute]
    • Y10T428/24967—Absolute thicknesses specified
    • Y10T428/24975—No layer or component greater than 5 mils thick
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/31504—Composite [nonstructural laminate]
    • Y10T428/31678—Of metal

Definitions

  • the present invention relates to a surface coated cutting tool (hereinafter referred to as a coated tool) in which a hard coating layer has excellent interlayer adhesion strength, and therefore chipping (fine fracturing) does not occur at cutting edges, and excellent cutting performance is exhibited over a long period of use even in a case where, for example, a work piece, such as steel or cast iron, is cut under high-speed intermittent cutting conditions in which high temperatures are generated, and, particularly, intermittent load is applied to the cutting edges.
  • a coated tool a surface coated cutting tool in which a hard coating layer has excellent interlayer adhesion strength, and therefore chipping (fine fracturing) does not occur at cutting edges, and excellent cutting performance is exhibited over a long period of use even in a case where, for example, a work piece, such as steel or cast iron, is cut under high-speed intermittent cutting conditions in which high temperatures are generated, and, particularly, intermittent load is applied to the cutting edges.
  • This coated tool is known to exhibit excellent wear resistance in a cutting process of steel, cast iron, and the like.
  • a coated tool in which the grain width of a TiCN layer composing a lower layer of a hard coating layer is set to 0.01 ⁇ m to 0.5 ⁇ m in order to improve the fracture resistance, impact resistance, wear resistance, and the like of the coated tool is known (for example, Patent Literature 2).
  • JPS57137460 discloses a cutting tool having a 0.8 micrometer thin alumina on top of 3 micrometer thick TiC-layer.
  • the nucleation alumina layer has a grain size of 0.1 micrometers.
  • the grain size of TiC is not specifically disclosed.
  • the grain size of the TiC layer is 0.4-0.5 micrometers.
  • the present inventors carried out thorough studies regarding the layer structure of a hard coating layer in order to improve the chipping resistance and delamination resistance of a coating tool, and, consequently, found the following.
  • the lower layer composed of a Ti compound layer formed of one or more layers of a TiC layer, a TiN layer, a TiCN layer, a TiCO layer, and a TiCNO layer contributes to improving the high-temperature strength of the hard coating layer by the intrinsic excellent high-temperature strength thereof.
  • the upper layer composed of an Al 2 O 3 layer is excellent in terms of oxidation resistance and thermal stability, and further has high hardness.
  • the adhesion strength between the lower layer and the upper layer is not sufficient in high-speed intermittent cutting in which high temperatures are generated, and high load is particularly intermittently applied to cutting edges, which may result in occurrence of fine chipping and interlayer delamination.
  • the average grain diameter of crystal grains in the Ti compound layer immediately below the Al 2 O 3 layer is set to 0.5 ⁇ m or less, and the lower and upper layers are vapor-deposited so that the ratio b1/a1 satisfies 4 ⁇ b1/a1 ⁇ 20, when a1 is the number of the crystal grain (Ti compound) on the lower layer side touching the interface between the first lower layer and the first upper layer, and b1 is the number of the crystal grain (Al 2 O 3 ) on the upper layer side touching the interface between the first lower layer and the first upper layer. Because of these, distortion occurring in the interface between the lower layer and the upper layer is alleviated. Consequently, the interlayer adhesion strength between the lower layer and the upper layer is increased.
  • the average grain diameter of the Ti compound layer composing a second lower layer immediately below the Al 2 O 3 layer is set to 0.1 ⁇ m or less, the second lower layer and the second upper layer are vapor-deposited on the cutting edge portion 1 so that the ratio b2/a2 saticefies 0.8 ⁇ b2/a2 ⁇ 1.2, when a2 is the number of the crystal grain (Ti compound) on the second lower layer side toughing the interface between the second lower layer and the second upper layer, and b2 is the number of the crystal grain (Al2O3) on the second upper layer side touching the interface between the second lower layer and the second upper layer, and the first lower layer and the first upper layer are vapor-deposited on the flank face portion 2 and the rake portion 3 so that the ratio b1/a1 satisfies 4 ⁇ b1/a1 ⁇ 20, when a1 is the number of the crystal grain (Ti compound) on the first lower layer side touching the interface between the first lower layer and the first upper layer, and b1 is
  • a first aspect is a surface coated cutting tool including: a cutting tool body made of tungsten carbide-based cemented carbide or titanium carbide-based cermet; and a first hard coating layer vapor-deposited on at least a part of the surface of the cutting tool body, wherein the first hard coating layer includes a first lower layer vapor-deposited on the surface of the cutting tool body, and a first upper layer vapor-deposited on the surface of the lower layer, wherein the first lower layer includes one or more Ti compound layers selected from a group consisting of a Ti carbide layer, a Ti nitride layer, a Ti carbonitride layer, a Ti carboxide layer, and a Ti oxycarbonitride layer; the first upper layer includes an Al 2 O 3 layer; a ratio of b1 to a1, which is b1/a1, satisfies the formula, 4 ⁇ b1/a1 ⁇ 20, a1 being the number of crystal grains on the Ti compound layer side touching the interface between the first lower layer and the first upper layer
  • the surface coated cutting tool according to the current invention as claimed in claim 1 further includes: a second hard coating layer vapor-deposited on a surface of a cutting edge portion 1 of the cutting tool body, when a tool area is divided into three areas composed of the cutting edge portion 1, a flank face portion 2, and a rake face portion 3, wherein the second hard coating layer includes: a second lower layer vapor-deposited on the surface of the cutting edge portion 1 of the cutting tool body; and a second upper layer vapor-deposited on the surface of the second lower layer, wherein the second lower layer includes one or more Ti compound layers selected from a group consisting of a Ti carbide layer, a Ti nitride layer, a Ti carbonitride layer, a Ti carboxide layer, and a Ti oxycarbonitride layer; the second upper layer includes an Al 2 O 3 layer with an ⁇ -type crystal structure; a ratio of b2 to a2, which is b2/a2, satisfies the formula, 0.8 ⁇ b2/a2 ⁇
  • the average overall layer thickness of the first lower layer may be 3 ⁇ m to 20 ⁇ m, and the average layer thickness of the first upper layer may be 1 ⁇ m to 15 ⁇ m.
  • the average overall layer thickness of the second lower layer may be 3 ⁇ m to 20 ⁇ m, and the average layer thickness of the second upper layer may be 1 ⁇ m to 15 ⁇ m.
  • an average diameter of crystal grains in the Ti compound layer, which is included in the first lower layer and located directly below the Al 2 O 3 layer of the first upper layer, may be 0.1 ⁇ m to 0.5 ⁇ m.
  • the first lower layer and the first upper layer included in the first hard coating layer of the first aspect will be explained in detail below.
  • the first lower layer is a Ti compound layer including one more layers of a Ti carbide (TiC) layer, a Ti nitride (TiN) layer, a Ti carbonitride (TiCN) layer, a Ti carboxide (TiCO) layer, and a Ti oxycarbonitride (TiCNO) layer.
  • the first lower layer is present as a lower layer of the first hard coating layer, and contributes to improving high-temperature strength of a hard coating layer by the intrinsic excellent high-temperature strength thereof. In a case in which the total average layer thickness of the first lower layer is less than 3 ⁇ m, the above-mentioned technical effect cannot be sufficiently exhibited.
  • the average layer thickness was specified as 3 ⁇ m to 20 ⁇ m.
  • a more preferable average layer thickness of the first lower layer is 5 ⁇ m to 15 ⁇ m.
  • An even more preferable average layer thickness of the first lower layer is 7 ⁇ m to 10 ⁇ m.
  • the average grain diameter of the crystal grains in the Ti compound layer immediately below the upper layer (Al 2 O 3 layer) exceeds 0.5 ⁇ m, the interlayer adhesion strength between the upper layer (Al 2 O 3 layer) and the Ti compound layer immediately below the upper layer (Al 2 O 3 layer) is weakened. As a result, the chipping resistance of the surface coated tool is deteriorated. Because of this, the average grain diameter of the crystal grains in the Ti compound layer immediately below the upper layer (Al 2 O 3 layer) was specified as 0.5 ⁇ m or less. The more preferable average grain diameter of the crystal grains in the Ti compound layer immediately below the upper layer (Al 2 O 3 layer) is 0.3 ⁇ m or less.
  • the average grain diameter is obtained by drawing a 50 ⁇ m-long line in the parallel direction to the surface of the carbide substrate on a cross section observed using a transmission electron microscope, counting the number of intersections with crystal grain boundaries of the crystal grains in the Ti compound layer immediately below the Al 2 O 3 layer, and obtaining a grain diameter from the average of the segment lengths.
  • the first upper layer is an Al 2 O 3 layer that is vapor-deposited on the surface of the first lower layer.
  • the first upper layer has high-temperature hardness and excellent heat resistance, and contributes to maintaining wear resistance as a fundamental role in a high-speed intermittent cutting process in which high temperatures are generated.
  • the Al 2 O 3 layer which satisfies conditions specified in the first aspect of the invention can be formed.
  • the pretreatment for vapor-deposition of Al 2 O 3 is composed of the following first to fourth steps.
  • the surface of the first lower layer is reformed under conditions described below.
  • the gas in a furnace is purged using Ar for 1 minute to 3 minutes in a state in which the following conditions below are maintained.
  • An oxidization treatment is carried out under conditions shown below (the proportion of CO 2 in the reaction gas is gradually decreased as the time elapses).
  • the gas in the furnace is purged using Ar for 1 minute to 3 minutes in a state in which the following conditions shown below are maintained.
  • the first upper layer having an interfacial structure in which the value of b1/a1 is 4 or more and 20 or less can be vapor deposited, when a1 is the number of crystal grains on the first lower layer side touching the interface between the first lower layer and the first upper layer, b1 is the number of crystal grains on the Al 2 O 3 layer side touching the interface between the first lower layer and the first upper layer in a cross-section vertical to the surface of the cutting tool body, and the ratio b1 to a1, which is b1/a1, is calculated.
  • the numbers of a1 and b1 can be obtained by counting Ti coupound grains having the interface with an Al 2 O 3 grain, and Al 2 O 3 grains having the interface with a Ti compound grain as explained below.
  • a cross section of the cutting tool is observed by performing a dark-field observation with a magnification of 50000 times at 10 points on the interface between the first lower layer and the first upper layer using a transmission electron microscope.
  • a 25 ⁇ m straight-line parallel to the surface of the carbide substrate is defined as the measurement width.
  • the 25 ⁇ m straight-lines are placed and the numbers of the Ti coupound grains having the interface with an Al 2 O 3 grain, and the numbers of Al 2 O 3 grains having the interface with a Ti compound grain are counted in the measurement width.
  • b1/a1 of the ratio of b1 to a1 is 4 or less, it becomes impossible to sufficiently alleviate misfit in the interface between the first lower layer and the first upper layer.
  • b1/a1 exceeds 20, the inter-grain stress in Al 2 O 3 is increased, and excellent interlayer adhesion strength cannot be exhibited. Because of these, b1/a1 was specified as 4 ⁇ b1/a1 ⁇ 20.
  • the first hard coating layer of the first aspect which includes the first upper layer and the first lower layer having the above interface configuration, interface distortion is alleviated, and therefore excellent interlayer adhesion strength is provided.
  • occurrence of fine chipping and occurrence of delamination are suppressed in a high-speed intermittent cutting process.
  • the average layer thickness of the first upper layer In a case in which the average layer thickness of the first upper layer is less than 1 ⁇ m, wear resistance cannot be sufficiently exhibited over a long period of use, and the tool life is shortened. On the other hand, when the average layer thickness of the first upper layer exceeds 15 ⁇ m, chipping, fracturing, delamination, and the like are liable to occur at the cutting edge portion 1. Because of these, the average layer thickness of the first upper layer was specified as 1 ⁇ m to 15 ⁇ m. A more preferable average layer thickness of the first upper layer is 3 ⁇ m to 12 ⁇ m. An even more preferable average layer thickness of the first upper layer is 5 ⁇ m to 10 ⁇ m.
  • the second lower layer is a Ti compound layer including one or more layers of a Ti carbide (TiC) layer, a Ti nitride (TiN) layer, a Ti carbonitride (TiCN) layer, a Ti carboxide (TiCO) layer, and a Ti oxycarbonitride (TiCNO) layer.
  • TiC Ti carbide
  • TiN Ti nitride
  • TiCN Ti carbonitride
  • TiCO Ti carboxide
  • TiCNO Ti oxycarbonitride
  • the average layer thickness was specified as 3 ⁇ m to 20 ⁇ m.
  • a more preferable average layer thickness of the second lower layer is 5 ⁇ m to 15 ⁇ m.
  • An even more preferable average layer thickness of the second lower layer is 7 ⁇ m to 10 ⁇ m.
  • the average grain diameter of the Ti compound layer immediately below the Al 2 O 3 layer exceeds 0.1 ⁇ m, the interlayer adhesion strength between the upper layer (Al 2 O 3 layer) and the Ti compound layer immediately below the upper layer (Al 2 O 3 layer) is weakened, and chipping resistance is deteriorated. Because of these, the average grain diameter in the Ti compound layer immediately below the Al 2 O 3 layer was specified as 0.1 ⁇ m or less in the second hard coating layer. In contrast to the cutting edge portion, the flank portion 2 and the cutting portion 3 may be coated with the first hard coating layer.
  • the average grain diameter in the Ti compound layer immediately below the Al 2 O 3 layer exceeds 0.5 ⁇ m in the flank portion 2 and the cutting portion 3, the interlayer adhesion strength between the upper layer (Al 2 O 3 layer) and the Ti compound layer immediately below the upper layer (Al 2 O 3 layer) is weakened, and chipping resistance is deteriorated.
  • the average grain diameter in the Ti compound layer immediately below the Al 2 O 3 layer is smaller than 0.1 ⁇ m, the crystal grains are coarsened, the high-temperature strength is degraded, and the fracture resistance, impact resistance, and wear resistance are degraded. Therefore, the average grain diameter in the Ti compound layer immediately below the Al 2 O 3 layer is preferably 0.1 ⁇ m to 0.5 ⁇ m.
  • a wet blast treatment was carried out only on the cutting edge portion 1, and the surface roughness Ra of the cutting edge portion 1 was set to 0.2 ⁇ m or less on the cutting tool body.
  • a polishing solution obtained by mixing 15% by mass to 60% by mass of aluminum oxide fine grains with respect to the total amount with water is sprayed as a spraying polishing solution.
  • the second upper layer is an Al 2 O 3 layer that is vapor-deposited on the surface of the second lower layer.
  • the second upper layer has high-temperature hardness and excellent heat resistance, and contributes to maintaining wear resistance as a fundamental role in a high-speed cutting process in which high load is intermittently exerted to the cutting edge.
  • the second lower layer including a Ti compound layer for example, a pretreatment for deposition of Al 2 O 3 is carried out in the following order. And then, an Al 2 O 3 layer is formed under ordinary conditions, whereby the Al 2 O 3 layer which satisfies conditions specified in the second aspect of the invention can be formed.
  • the pretreatment for vapor-deposition of Al 2 O 3 is composed of the following first to fourth steps.
  • the surface of the second lower layer is reformed under conditions described below.
  • the gas in a furnace is purged using Ar for 1 minute to 3 minutes in a state in which the following conditions below are maintained.
  • An oxidization treatment is carried out under conditions shown below (the proportion of CO 2 in the reaction gas is gradually decreased as the time elapses).
  • the gas in the furnace is purged using Ar for 1 minute to 3 minutes in a state in which the following conditions shown below are maintained.
  • the second hard coating layer having an interfacial structure in which the value of b2/a2 is 0.8 or more and 1.2 or less can be vapor deposited on the cutting edge portion 1, when a2 is the number of crystal grains on the second lower layer side touching the interface between the second lower layer and the second upper layer, b2 is the number of crystal grains on the Al 2 O 3 layer side touching the interface between the second lower layer and the second upper layer in a cross-section vertical to the surface of the cutting tool body, and the ratio b2 to a2, which is b2/a2, is calculated.
  • b2/a2 of the ratio of b2 to a2 is 0.8 or less, it becomes impossible to sufficiently alleviate misfit in the interface between the first lower layer and the first upper layer in the cutting edge portion 1.
  • b2/a2 exceeds 1.2, the inter-grain stress in Al 2 O 3 is increased, and excellent interlayer adhesion strength cannot be exhibited. Because of these, b2/a2 was specified as 0.8 ⁇ b2/a2 ⁇ 1.2.
  • the numbers of a2 and b2 can be obtained by counting Ti coupound grains having the interface with an Al 2 O 3 grain, and Al 2 O 3 grains having the interface with a Ti compound grain as explained below.
  • a cross section of the cutting tool is observed by performing a dark-field observation with a magnification of 50000 times at 10 points on the interface between the second lower layer and the second upper layer using a transmission electron microscope.
  • a 25 ⁇ m straight-line parallel to the surface of the carbide substrate is defined as the measurement width.
  • the 25 ⁇ m straight-lines are placed and the numbers of the Ti coupound grains having the interface with an Al 2 O 3 grain, and the numbers of Al 2 O 3 grains having the interface with a Ti compound grain are counted in the measurement width.
  • the second hard coating layer according to the present invention which includes the second upper layer and the second lower layer having the above interface configuration, interface distortion is alleviated, and therefore excellent interlayer adhesion strength is provided.
  • occurrence of fine chipping and occurrence of delamination are suppressed in a high-speed intermittent cutting process.
  • the average layer thickness of the second upper layer In a case in which the average layer thickness of the second upper layer is less than 1 ⁇ m, wear resistance cannot be sufficiently exhibited over a long period of use, and the tool life is shortened. On the other hand, when the average layer thickness of the second upper layer exceeds 15 ⁇ m, chipping, fracturing, delamination, and the like are liable to occur at the cutting edge portion 1. Because of these, the average layer thickness of the second upper layer was specified as 1 ⁇ m to 15 ⁇ m. A more preferable average layer thickness of the second upper layer is 3 ⁇ m to 12 ⁇ m. An even more preferable average layer thickness of the second upper layer is 5 ⁇ m to 10 ⁇ m.
  • the coated tool of the first aspect is a cutting tool, which has the vapor-deposited first lower layer including a Ti compound layer and the vapor-deposited first upper layer including Al 2 O 3 layer, as the hard coating layer.
  • the interface structure is configured so that b1/a1 satisfies 4 ⁇ b1/a1 ⁇ 20.
  • b1/a1 is the ratio of b1 to a1.
  • the value of a1 is the number of Ti compound crystal grains on the first lower layer side touching the interface between the first lower layer and the first upper layer.
  • the value of b1 is the number of Al 2 O 3 crystal grains on the first upper layer side touching the interface between the first lower layer and the first upper layer.
  • the average grain diameter of crystal grains in the Ti compound layer immediately below the first upper layer is set to 0.5 ⁇ m or less.
  • the interlayer adhesion strength between the first lower layer and the first upper layer can be particularly increased.
  • the coated tool is used in a high-speed intermittent cutting process in which high temperatures are generated, and high load is applied on the cutting edge, for example, a high-speed intermittent cutting process on steel, cast iron, or the like
  • the hard coating layer has excellent interlayer adhesion strength, and therefore occurrence of fine chipping, delamination, and the like at cutting edges is reduced.
  • the coated tool of the first aspect exhibits excellent wear resistance over a long period of use.
  • the coated tool of the invention is a tool further having the second hard layer in addition to the first hard coating layer.
  • the second hard layer has the vapor-deposited second lower layer including an Ti compound layer and the vapor-deposited second upper layer including Al 2 O 3 layer.
  • the interface structure is configured so that b2/a2 satisfied 0.8 ⁇ b2/a2 ⁇ 1.2.
  • the value of a2 is the number of Ti compound crystal grains on the second lower layer side touching the interface between the second lower layer and the second upper layer.
  • the value of b2 is the number of Al 2 O 3 crystal grains on the second upper layer side touching the interface between the second lower layer and the second upper layer.
  • the average grain diameter of crystal grains in the Ti compound layer immediately below the Al 2 O 3 layer is set to 0.1 ⁇ m or less.
  • the interface structure is configured so that b1/a1 satisfies 4 ⁇ b1/a1 ⁇ 20.
  • b1/a1 is the ratio of b1 to a1.
  • the value of a1 is the number of Ti compound crystal grains on the first lower layer side touching the interface between the first lower layer and the first upper layer.
  • the value of b1 is the number of Al 2 O 3 crystal grains on the first upper layer side touching the interface between the first lower layer and the first upper layer.
  • the average grain diameter of crystal grains in the Ti compound layer immediately below the first upper layer is set to 0.1 ⁇ m to 0.5 ⁇ m.
  • the interlayer adhesion strength between the first lower layer and the first upper layer can be particularly increased.
  • the coated tool is used in a high-speed intermittent cutting process in which high temperatures are generated, and high load is intermittently applied to the cutting edge portion 1, for example, a high-speed intermittent cutting process on steel, cast iron, or the like, the hard coating layer has excellent interlayer adhesion strength, and therefore occurrence of fine chipping, delamination, and the like at the cutting edge portion 1 is reduced.
  • the coated tool of the invention can exhibits excellent wear resistance over a long period of use.
  • WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder, TiN powder, TaN powder, and Co powder were prepared, and the raw material powder was mixed into the mixture compositions as shown in Table 1.
  • wax was added to the mixture, mixed in acetone for 24 hours using a ball mill, dried under reduced pressure, and then pressed into a green compact having a predetermined shape at a pressure of 98 MPa.
  • the green compact was vacuum-sintered under conditions in which the green compact was held at a predetermined temperature in a range of 1370°C to 1470°C under a vacuum of 5 Pa for 1 hour.
  • a honing process with R: 0.07 mm was carried out on the cutting edge portion, and cutting tool bodies 1 A to 1F made of a WC-based cemented carbide having an insert shape, which is defined in ISO CNMG 160412, were manufactured.
  • TiCN (TiC/TiN 50/50 by the mass ratio) powder, Mo 2 C powder, ZrC powder, NbC powder, TaC powder, WC powder, Co powder, and Ni powder, all of which had an average grain diameter of 0.5 ⁇ m to 2 ⁇ m, were used.
  • the raw material powder was mixed into the mixture compositions as shown in Table 2, wet-mixed for 24 hours using a ball mill, dried, and then pressed into a green compact at a pressure of 98 MPa.
  • the green compact was held in a nitrogen atmosphere of 1.3 kPa under conditions of a temperature of 1540°C for 1 hour, and sintered.
  • each of the cutting tool bodies 1A to 1F and the cutting tool bodies 1a to 1f was placed in an ordinary chemical vapor deposition apparatus, and Ti compound layers having the combinations and the target layer thicknesses as shown in Table 6 were formed by vapor-deposition as the first lower layer of the first hard coating layer under conditions as shown in Table 3 (1-TiCN in Table 3 represents forming conditions of a TiCN layer having the columnar crystal structure as described in JP-A-H6-8010 , and the others represent forming conditions of an ordinary granular crystal structure).
  • Al 2 O 3 layers were vapor-deposited as the first upper layer to produce the surface coated tools A1 to A13 of the present invention.
  • the condition for the vapor-deposition is shown in Table 3.
  • Combinations of cutting tool bodies, the lower layer and the upper layer are shown in Table 5.
  • the target layer thickness of the upper layer is shown in Table 5.
  • the conventional surface coated tools A1 to A13 shown in Table 6 were also manufactured.
  • the conventional surface coated tools A1 to A13 were produced in the same way to the surface coated tools A1 to A13 of the present invention by vapor-depositing the first lower layer (Ti compound layer) and the first upper layer (Al 2 O 3 layer), except for not performing the pretreatment prior to Al 2 O 3 vapor-deposition on the surface of the lower layer.
  • Table 5 shows a1 and b1 obtained by the above measurement, and the values of b1/a1 obtained therefrom.
  • FIG. 2 shows a schematic view of an interface structure of the interface between the first lower layer and the first upper layer of the surface coated tool A6.
  • the schematic view was prepared based on a transmission electron microscopic photograph, and values of a1, b1, and b1/a1.
  • FIG. 3 shows a schematic view of an interface structure of the interface between the first lower layer and the first upper layer of the conventional surface coated tool A8.
  • the schematic view was prepared using a transmission electron microscopic photograph, and values of a1, b1, and b1/a1.
  • Table 5 shows the measured average grain diameters.
  • the thicknesses of component layers of the hard coating layers of the surface coated tools A1 to A13 and the conventional surface coated tools A1 to A13 were measured (vertical cross section measurement) using a scanning electron microscope. Based on the results, all the thicknesses of the component layers of the hard coating layers had the average layer thickness (average value of 5 point-measurement), which was substantially the same as the target layer thickness.
  • a dry high-speed intermittent cutting test (an ordinary cutting speed is 200 m/min.) of nickel chrome molybdenum steel was carried out under conditions below.
  • a dry high-speed intermittent cutting test (an ordinary cutting speed is 180 m/min.) of cast iron was carried out under conditions below.
  • a dry high-speed intermittent cutting test (an ordinary cutting speed is 250 m/min.) of carbon steel was carried out under conditions below.
  • the surface coated tools A1 to A13 had the interface structures satisfying 4 ⁇ b1/a1 ⁇ 20, when b1/a1 is the ratio of b1 to a1.
  • a1 was the number of Ti compound crystal grains in the lower layer side touching the interface between the first lower layer and the first upper layer.
  • b1 was the number of Al 2 O 3 crystal grains in the upper layer side touching the interface between the first lower layer and the first upper layer. It was also demonstrated that the average grain diameter of crystal grains in the Ti compound layer immediately below the upper layer (Al 2 O 3 layer) was 0.5 ⁇ m or less.
  • WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder, TiN powder, TaN powder, and Co powder all of which had an average grain diameter of 2 ⁇ m to 4 ⁇ m, were prepared, and the raw material powder was mixed into the mixture compositions as shown in Table 8. Next, wax was added to the mixture, mixed in acetone for 24 hours using a ball mill, dried under reduced pressure, and then pressed into a green compact having a predetermined shape at a pressure of 98 MPa.
  • the compact was vacuum-sintered under conditions in which the compact was held at a predetermined temperature in a range of 1370°C to 1470°C under a vacuum of 5 Pa for 1 hour.
  • a honing process with R: 0.07 mm was carried out on the cutting edge portion, and cutting tool bodies 2A to 2F made of a WC-based cemented carbide having an insert shape, which is defined in ISO CNMG 160412, were manufactured.
  • TiCN (TiC/TiN 50/50 by the mass ratio) powder, Mo 2 C powder, ZrC powder, NbC powder, TaC powder, WC powder, Co powder, and Ni powder, all of which had an average grain diameter of 0.5 ⁇ m to 2 ⁇ m, were used.
  • the raw material powder was mixed into the mixture compositions as shown in Table 9, wet-mixed for 24 hours using a ball mill, dried, and then pressed into a green compact at a pressure of 98 MPa.
  • the green compact was held in a nitrogen atmosphere of 1.3 kPa under conditions of a temperature of 1540°C for 1 hour, and sintered.
  • cutting tool bodies 2a to 2f made of a TiCN-based cermet having an insert shape, which is defined in ISO CNMG 160412, were formed.
  • portions other than the cutting edge portion 1 were covered with a hard urethane rubber or the like, and a wet blast treatment was carried out only on the cutting edge portion 1 by spraying a polishing solution in which 15% by mass to 60% by mass of Al 2 O 3 fine grains was mixed with respect to the total amount with water.
  • the cutting tool bodies 2A to 2F and the cutting tool bodies 2a to 2f were placed in an ordinary chemical vapor deposition apparatus, and Ti compound layers having the combinations and the target layer thicknesses as shown in Table 12 were formed by vapor-deposition as the second lower layer of the second hard coating layer under conditions as shown in Table 10
  • (1-TiCN in Table 10 represents forming conditions of a TiCN layer having the columnar crystal structure as described in JP-A-H6-8010 , and the others represent forming conditions of an ordinary granular crystal structure).
  • Al 2 O 3 layers having the combinations and the target layer thicknesses as shown in Table 12 were formed by vapor-deposition as the second upper layer under the conditions as shown in Table 10, and the surface coated tools B1 to B13 of the present invention were manufactured.
  • the conventional surface coated tools B1 to B13 shown in Table 13 were also manufacture.
  • the conventional surface coated tools B1 to B13 were produced in the same way to the surface coated tools B1 to B13 of the present invention by vapor-depositing the lower layer (Ti compound layer) and the upper layer (Al 2 O 3 layer), except for not performing the pretreatment prior to Al 2 O 3 vapor-deposition on the surface of the lower layer.
  • Tables 12 and 13 show values of a1, b1, b1/a1, a2, b2, and b2/a2 obtained by the above measurement. Since it was confirmed that the values of a1, b1, and b1/a1 of the flank face portion 2 and the rake face portion 3 were almost the same in all of the coated tools, only the values in the flank face portion 2 were shown, and the values of the cutting portion 3 were not shown.
  • FIG. 1 shows the cutting edge portion 1, the flank face portion 2, and the rake face portion 3 using a cross-sectional view of the cutting tool.
  • the cutting tool portion 1 includes an area that firstly comes into contact with a work piece in a cutting process, and is constituted by a curved surface present between the flank faces and the rake face in the cutting tool.
  • FIG. 4 shows a schematic view of an interface structure of an interface between the second lower layer and the second upper layer at the cutting edge portion 1 of the surface coated tool B1 of the present invention.
  • the schematic view was prepared using a transmission electron microscopic photograph.
  • FIG. 5 shows a schematic view of an interface structure of the interface between the first lower layer and the first upper layer at the flank face portion 2 of the surface coated tool B1 of the present invention.
  • the schematic view was prepared using a transmission electron microscopic photograph.
  • FIG. 6 shows a schematic view of an interface structure of the interface between the second lower layer and the second upper layer at the cutting edge portion 1 of the conventional surface coated tool B 1.
  • the schematic view was prepared using a transmission electron microscopic photograph.
  • FIG. 7 shows a schematic view of an interface structure of the interface between the first lower layer and the first upper layer at the flank face portion 2 of the conventional surface coated tool B1.
  • the schematic view was prepared using a transmission electron microscopic photograph.
  • a 50 ⁇ m-long line was drawn in the parallel direction to the surface of the carbide substrate on a cross section observed using a transmission electron microscope. Then, the number of intersections with crystal grain boundaries of the crystal grains in the Ti compound layer immediately below the Al 2 O 3 layer was counted, and an average grain diameter was obtained from the average intervals of the segments.
  • Table 12 shows the measured average grain diameters.
  • the thicknesses of component layers of the hard coating layers of the surface coated tools B1 to B13 of the present invention and the conventional surface coated tools B1 to B13 were measured (vertical cross section measurement) using a scanning electron microscope. Based on the results, all the thicknesses of the component layers of the hard coating layers had the average layer thickness (average value of 5 point-measurement), which was substantially the same as the target layer thickness.
  • a dry high-speed intermittent cutting test (an ordinary cutting speed is 200 m/min.) of nickel chrome molybdenum steel was carried out under conditions below.
  • a dry high-speed intermittent cutting test (an ordinary cutting speed is 180 m/min.) of cast iron was carried out under conditions below.
  • a dry high-speed intermittent cutting test (an ordinary cutting speed is 250 m/min.) of carbon steel was carried out under conditions below.
  • the surface coated tools B1 to B13 of the present invention had the interface structure satisfying 0.8 ⁇ b2/a2 ⁇ 1.2 on the cutting edge portion 1, when b2/a2 was the ratio of b2 to a2.
  • a2 was the number of Ti compound crystal grains in the second lower layer side touching the interface between the second lower layer and the second upper layer.
  • b2 was the number of Al 2 O 3 crystal grains in the second upper layer side touching the interface between the second lower layer and the second upper layer. It was also demonstrated that the average grain diameter of crystal grains of crystal grains in the Ti compound layer immediately below the Al 2 O 3 layer was 0.1 ⁇ m or less.
  • the surface coated tools B1 to B13 of the present invention had the interface structures satisfying 4 ⁇ b1/a1 ⁇ 20 on the flank face portion 2 and rake face portion 3, when b1/a1 is the ratio of b1 to a1.
  • a1 was the number ofTi compound crystal grains in the lower layer side touching the interface between the first lower layer and the first upper layer.
  • b1 was the number of Al 2 O 3 crystal grains in the upper layer side touching the interface between the first lower layer and the first upper layer. It was also demonstrated that the average grain diameter of crystal grains in the Ti compound layer immediately below the upper layer (Al 2 O 3 layer) was 0.1 ⁇ m to 0.5 ⁇ m.
  • the coated tool of the present invention shows excellent chipping resistance and wear resistance against steel, cast iron, and the like, particularly in high-speed intermittent cutting processes in which high temperatures are generated, and high load is applied to cutting edges, and exhibits excellent cutting performance over a long period of use, performance improvement of cutting apparatuses, power saving and energy saving of cutting processes, and, furthermore, cost reduction can be sufficiently expected.

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Claims (4)

  1. Outil de coupe revêtu en surface comprenant :
    un corps d'outil de coupe réalisé en carbure cémenté à base de carbure de tungstène ou en cermet à base de carbure de titane ;
    une première couche de revêtement dure déposée en phase vapeur sur au moins une partie de la surface du corps d'outil de coupe ; et
    une deuxième couche de revêtement dure déposée en phase vapeur sur la surface de la partie de bord de coupe (1) du corps d'outil de coupe, où une zone d'outil est divisée en trois zones composées de la partie de bord de coupe (1), d'une partie de face de dépouille (2), et d'une partie de face de coupe (3), dans lequel
    la première couche de revêtement dure comprend une première couche inférieure déposée en phase vapeur sur la surface du corps d'outil de coupe, et
    une première couche supérieure déposée en phase vapeur sur la surface de la couche inférieure, dans lequel
    la première couche inférieure comprend une ou plusieurs couche(s) de composé de Ti choisie(s) dans le groupe constitué d'une couche de carbure de Ti, d'une couche de nitrure de Ti, d'une couche de carbonitrure de Ti, d'une couche de carboxyde de Ti et d'une couche d'oxycarbonitrure de Ti ;
    la première couche supérieure comprend une couche d'Al2O3 ;
    le rapport de b1 sur a1, qui s'écrit b1/a1 satisfait la formule, 4 ≤ b1/a1 ≤ 20, a1 étant le nombre de grains cristallins sur le côté de couche de composé de Ti touchant l'interface entre la première couche inférieure et la première couche supérieure, et b1 étant le nombre de grains cristallins sur le côté de couche d'Al2O3 touchant l'interface entre la première couche inférieure et la première couche supérieure ; et
    un diamètre moyen de grains cristallins dans la couche de composé de Ti se trouvant directement en dessous de la couche d'Al2O3 de la première couche supérieure est inférieur ou égal à 0,5 µm, où
    la deuxième couche de revêtement dure comprend : une deuxième couche inférieure déposée en phase vapeur sur la surface de la partie de bord de coupe du corps d'outil de coupe ; et
    une deuxième couche supérieure déposée en phase vapeur sur la surface de la deuxième couche inférieure, où
    la deuxième couche inférieure comprend une ou plusieurs couche(s) de composé de Ti choisie(s) dans le groupe constitué d'une couche de carbure de Ti, d'une couche de nitrure de Ti, d'une couche de carbonitrure de Ti, d'une couche de carboxyde de Ti et d'une couche d'oxycarbonitrure de Ti;
    la deuxième couche supérieure comprend une couche d'Al2O3 ayant une structure cristalline de type α ;
    le rapport de b2 sur a2, qui s'écrit b2/a2, satisfait la formule : 0,8 ≤ b2/a2 ≤ 1,2, a2 étant le nombre de grains cristallins sur le côté de couche de composé de Ti touchant l'interface entre la deuxième couche inférieure et la deuxième couche supérieure, et b2 étant le nombre de grains cristallins sur le côté de couche d'Al2O3 touchant l'interface entre la deuxième couche inférieure et la deuxième couche supérieure ;
    un diamètre moyen de grains cristallins dans la couche de composé de Ti se trouvant directement en dessous de la couche d'Al2O3 de la deuxième couche supérieure est inférieur ou égal à 0,1 µm, et
    la partie de face de dépouille (2) et la partie de face de coupe (3) sont revêtues de la première couche de revêtement dure.
  2. Outil de coupe revêtu en surface selon la revendication 1,
    dans lequel l'épaisseur de couche totale moyenne de la première couche inférieure est de 3 µm à 20 µm, et
    l'épaisseur de couche moyenne de la première couche supérieure est de 1 µm à 15 µm.
  3. Outil de coupe revêtu en surface selon la revendication 1 ou 2,
    dans lequel l'épaisseur de couche totale moyenne de la deuxième couche inférieure est de 3 µm à 20 µm, et
    l'épaisseur de couche moyenne de la deuxième couche supérieure est de 1 µm à 15 µm.
  4. Outil de coupe revêtu en surface selon la revendication 2 ou 3,
    dans lequel le diamètre moyen de grains cristallins dans la couche de composé de Ti, qui est incluse dans la première couche inférieure et située directement en dessous de la couche d'Al2O3 de la première couche supérieure, est de 0,1 µm à 0,5 µm.
EP10826897.0A 2009-10-30 2010-11-01 Outil de coupe revêtu en surface avec excellente résistance à l'écaillage Active EP2495057B1 (fr)

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PCT/JP2010/069420 WO2011052767A1 (fr) 2009-10-30 2010-11-01 Outil de coupe revêtu en surface avec excellente résistance à l'écaillage

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JP5279099B1 (ja) * 2012-03-14 2013-09-04 住友電工ハードメタル株式会社 切削工具
KR101536462B1 (ko) * 2013-12-23 2015-07-24 한국야금 주식회사 난삭재 및 주철가공 절삭공구용 피막
JP6634647B2 (ja) * 2014-11-27 2020-01-22 三菱マテリアル株式会社 耐チッピング性、耐摩耗性にすぐれた表面被覆切削工具
CN111867760B (zh) * 2018-01-29 2023-04-07 京瓷株式会社 涂层刀具和具备它的切削刀具
KR102676439B1 (ko) * 2018-11-29 2024-06-19 교세라 가부시키가이샤 피복 공구 및 그것을 구비한 절삭 공구
JPWO2020250499A1 (fr) * 2019-06-13 2020-12-17
KR102297711B1 (ko) * 2019-12-20 2021-09-03 한국야금 주식회사 경질 피막이 형성된 절삭공구

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WO2011052767A1 (fr) 2011-05-05
CN102596456A (zh) 2012-07-18
KR101757489B1 (ko) 2017-07-12
EP2495057A1 (fr) 2012-09-05
US8758907B2 (en) 2014-06-24
EP2495057A4 (fr) 2014-11-05
CN102596456B (zh) 2014-12-10
US20120269589A1 (en) 2012-10-25
KR20140015132A (ko) 2014-02-06

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